STABILIZED ACID AND ALKALI RESISTANT Ni-Cr-Mo-Co ALLOYS

ABSTRACT

A nickel-chromium-molybdenum-copper alloy resistant to 70% sulfuric acid at 93° C. and 50% sodium hydroxide at 121° C. for acid and alkali neutralization in the field of waste management; the alloy contains, in weight percent, 27 to 33 chromium, 4.9 to 7.8 molybdenum, greater than 3.1 but no more than 6.0 copper, up to 3.0 iron, 0.3 to 1.0 manganese, 0.1 to 0.5 aluminum, 0.1 to 0.8 silicon, 0.01 to 0.11 carbon, up to 0.13 nitrogen, up to 0.05 magnesium, up to 0.05 rare earth elements, with a balance of nickel and impurities. Titanium or another MC carbide former can be added to enhance thermal stability of the alloy.

FIELD OF INVENTION

This invention relates generally to non-ferrous alloy compositions, andmore specifically to nickel-chromium-molybdenum-copper alloys thatprovide a useful combination of resistance to 70% sulfuric acid at 93°C. and resistance to 50% sodium hydroxide at 121° C.

BACKGROUND

In the field of waste management, there is a need for metallic materialswhich resist hot, strong acids and hot, strong caustic alkalis. This isbecause such chemicals are used to neutralize one another, resulting inmore stable and less hazardous compounds. Of the acids used in industry,sulfuric is the most important in terms of the quantities produced. Ofthe caustic alkalis, sodium hydroxide (caustic soda) is the mostcommonly used.

Certain nickel alloys are very resistant to strong, hot sulfuric acid.Others are very resistant to hot, strong sodium hydroxide. However, nonepossesses adequate resistance to both chemicals.

Typically, nickel alloys with high alloy contents are used to resistsulfuric acid and other strong acids, the most resistant being thenickel-molybdenum and nickel-chromium-molybdenum alloys.

On the other hand, pure nickel (UNS NO2200/Alloy 200) or nickel alloyswith low alloy contents are the most resistant to sodium hydroxide.Where higher strength is required, the nickel-copper and nickel-chromiumalloys are used. In particular, alloys 400 (Ni—Cu, UNS N04400) and 600(Ni—Cr, UNS N06600) possess good resistance to corrosion in sodiumhydroxide.

During the discovery of the alloys of this invention, two keyenvironments were used, namely 70 wt. % sulfuric acid at 93° C. (200°F.) and 50 wt. % sodium hydroxide at 121° C. (250° F.). 70 wt. %sulfuric acid is well known to be very corrosive to metallic materials,and is the concentration at which the resistance of many materials(including the nickel-copper alloys) breaks down, as a result of changesin the cathodic reaction (from reducing to oxidizing). 50 wt. % sodiumhydroxide is the concentration most widely used in industry. A highertemperature was used in the case of sodium hydroxide to increaseinternal attack (the main form of degradation of nickel alloys in thischemical), hence increase the accuracy of measurements during subsequentcross-sectioning and metallographic examination.

In U.S. Pat. No. 6,764,646 Crook et al. describenickel-chromium-molybdenum-copper alloys resistant to sulfuric acid andwet process phosphoric acid. These alloys require copper in the range1.6 to 2.9 wt. %, which is below the levels required for resistance to70% sulfuric acid at 93° C. and 50% sodium hydroxide at 121° C.

U.S. Pat. No. 6,280,540 to Crook discloses copper-containing,nickel-chromium-molybdenum alloys which have been commercialized asC-2000® alloy and correspond to UNS N06200. These contain highermolybdenum levels and lower chromium levels than in the alloys of thisinvention and lack the aforementioned corrosion characteristics.

U.S. Pat. No. 6,623,869 to Nishiyama et al. describesnickel-chromium-copper alloys for metal dusting service at hightemperatures, the maximum copper contents of which are 3 wt. %. This isbelow the range required for resistance to 70% sulfuric acid at 93° C.and 50% sodium hydroxide at 121° C. More recent U.S. Patent ApplicationPublications (US 2008/0279716 and US 2010/0034690) by Nishiyama et al.describe additional alloys for resistance to metal dusting andcarburization. The alloys of US 2008/0279716 differ from the alloys ofthis invention in that they have a molybdenum restriction of not morethan 3%. The alloys of US 2010/0034690 are in a different class, beingiron-based, rather than nickel-based, with a molybdenum content of 2.5%or less.

SUMMARY OF THE INVENTION

The principal object of this invention is to provide alloys, capable ofbeing processed into wrought products (sheets, plates, bars, etc.),which exhibit a useful and elusive combination of resistance to 70%sulfuric acid at 93° C. (200° F.) and resistance to 50% sodium hydroxideat 121° C. (250° F.). These highly desirable properties have beenunexpectedly attained using a nickel base, chromium between 27 and 33wt. %, molybdenum between 4.9 and 7.8 wt. %, and copper greater than 3.1wt. % and up to 6.0 wt. %.

To enable the removal of oxygen and sulfur during the melting process,such alloys typically contain small quantities of aluminum and manganese(up to about 0.5 and 1.0 wt. %, respectively in thenickel-chromium-molybdenum alloys), and possibly traces of magnesium andthe rare earth elements (up to about 0.05 wt. %). In our experiments,aluminum contents of between 0.1 and 0.5 wt. %, and manganese contentsbetween 0.3 and 1.0 wt. %, were found to result in successful alloys.

Iron is the most likely impurity in such alloys, due to contaminationfrom other nickel alloys melted in the same furnaces, and maxima of 2.0or 3.0 wt. % are typical of those nickel-chromium-molybdenum alloys thatdo not require an iron addition. In our experiments, iron contents up to3.0 wt. % were found to be acceptable.

Other metallic impurities are possible in such alloys, due to furnacecontamination and impurities in the charge materials. The alloys of thisinvention should be able to tolerate these impurities at the levelscommonly encountered in the nickel-chromium-molybdenum alloys. Also,alloys of such high chromium content cannot be air melted without somepick up of nitrogen. It is usual, therefore, in high chromium nickelalloys to allow up to 0.13 wt. % maximum of this element.

With regard to carbon content, the successful alloys in our experimentscontained between 0.01 and 0.11 wt. %. Surprisingly, Alloy G with acarbon content of 0.002 wt. % could not be processed into wroughtproducts. Thus a carbon range of 0.01 to 0.11 wt. % is preferred.

With regard to silicon, a range of 0.1 to 0.8 wt. % is preferred, basedon the fact that levels at each end of this range provided satisfactoryproperties.

The microstructural stabilities of these alloys at elevated temperaturescan be improved by encouraging the formation of MC carbides, which arevery stable.

DETAILED DESCRIPTION OF THE INVENTION

The discovery of the compositional range defined above involved study ofa wide range of nickel-based compositions, of varying chromium,molybdenum, and copper contents. These compositions are presented inTable 1. For comparison, the compositions of the commercial alloys usedto resist either 70% sulfuric acid or 50% sodium hydroxide are includedin Table 1.

TABLE 1 Compositions of Experimental and Commercial Alloys Alloy Ni CrMo Cu Fe Mn Al Si C Other A* Bal. 27 7.8 6.0 1.1 0.3 0.2 0.1 0.03 B*Bal. 27 7.5 5.9 1.1 0.3 0.3 0.1 0.01 C Bal. 28 7.3 3.1 1.1 0.3 0.3 0.10.01 D Bal. 30 8.2 2.6 0.9 0.3 0.5 0.1 0.03 E* Bal. 29 6.6 4.7 0.9 0.40.1 0.3 0.01 F* Bal. 30 6.6 4.8 3.0 1.0 0.5 0.8 0.11 G Bal. 29 6.6 4.8 0.04 <0.01 <0.01 <0.01  0.002 H* Bal. 31 4.9 5.9 0.9 0.5 0.4 0.3 0.03I* Bal. 31 5.2 4.5 1.2 0.4 0.4 0.3 0.04 J Bal. 31 5.7 2.7 1.1 0.4 0.20.3 0.03 K Bal. 31 5.0 10.0  1.0 0.4 0.4 0.3 0.03 L Bal. 30 5.6 8.2 1.00.5 0.2 0.5 0.03 M Bal. 31 8.9 2.5 1.0 0.5 0.2 0.4 0.03 N Bal. 31 5.13.1 1.2 0.3 0.4 0.1 0.02 O* Bal. 33 5.6 4.5 1.0 0.4 0.2 0.3 0.03 P* Bal.30 6.9 4.8 <0.05 0.4 0.3 0.4 0.03 Q* Bal. 31 5.5 4.0 1.0 0.5 0.3 0.40.03 R* Bal. 30 5.4 4.0 1.0 0.5 0.3 0.4 0.07 S* Bal. 31 5.6 3.8 0.9 0.40.3 0.4 0.06 200** 99.0 min — — 0.1 0.2 0.2 — 0.2 0.08 (Ni + Co) 400**66.5 — — 31.5  1.2 1.0 — 0.2 0.2  Ni + Trace Co 600** 76.0 15.5 — 0.28.0 0.5 — 0.2 0.08 C-4** 65.0 16.0 16.0 0.5 3.0 1.0 —  0.08 0.01 Ti 0.7max max max max max max C-22** 56.0 22.0 13.0 0.5 3.0 0.5 —  0.08 0.01 W3.0 max max max max V 0.35 max C-276** 57.0 16.0 16.0 0.5 5.0 1.0 — 0.08 0.01 W 4.0 max max max max V 0.35 max C-2000** 59.0 23.0 16.0 1.63.0 0.5 0.5  0.08 0.01 max max max max max G-30** 43.0 30.0 5.5 2.015.0  1.5 — 0.8 0.03 Co 5.0 max max max max Nb 0.8 W 2.5 max G-35** 58.033.2 8.1 0.3 2.0 0.5 0.4 0.6 0.05 W 0.6 max max max max max max max*denotes an alloy of this invention, **denotes a nominal composition

The experimental alloys were made by vacuum induction melting (VIM),then electro-slag re-melting (ESR), at a heat size of 13.6 kg. Traces ofnickel-magnesium and/or rare earths were added to the VIM furnacecharges, to help minimize the sulfur and oxygen contents of theexperimental alloys. The ESR ingots were homogenized, hot forged, andhot rolled into sheets of thickness 3.2 mm for test. Surprisingly, threeof the alloys (G, K, and L) cracked so badly during forging that theycould not be hot rolled into sheets for testing. Those alloys which weresuccessfully rolled to the required test thickness were subjected toannealing trials, to determine (by metallographic means) the mostsuitable annealing treatments. Fifteen minutes at temperatures between1121° C. and 1149° C., followed by water quenching were determined to beappropriate, in all cases. The commercial alloys were all tested in thecondition sold by the manufacturer, the so-called “mill annealed”condition.

Corrosion tests were performed on samples measuring 25.4×25.4×3.2 mm.Prior to corrosion testing, surfaces of all samples were manually groundusing 120 grit papers, to negate any surface layers and defects thatmight affect corrosion resistance. The tests in sulfuric acid werecarried out in glass flask/condenser systems. The tests in sodiumhydroxide were carried out in TEFLON systems, since glass is attacked bysodium hydroxide. A time of 96 hours was used for the sulfuric acidtests, with interruptions every 24 hours to enable samples to beweighed, while a duration of 720 hours was used for the sodium hydroxidetests. Two samples of each alloy were tested in each environment, andthe results averaged.

In sulfuric acid, the primary mode of degradation is uniform attack,thus average corrosion rates were calculated from weight lossmeasurements. In sodium hydroxide, the primary mode of degradation isinternal attack, which is either a uniform attack or more aggressiveform of internal “dealloying” attack. Dealloying generally refers to theleaching of certain elements (for example, molybdenum) from the alloy,which often degrades the mechanical properties as well. The maximuminternal attack can only be measured by sectioning the samples andstudying them metallographically. The values presented in Table 2represent measured maximum internal penetration in the alloycross-section.

A pass/fail criterion of 0.5 mm/y (the generally acknowledged limit forindustrial service) was applied to the test results in bothenvironments.

Table 2 reveals that alloys of the present invention corrode at lowenough rates in 70% sulfuric acid to be useful industrially at 93° C.and exhibit internal penetration rates that correspond to significantlyless than 0.5 mm/y in 50% sodium hydroxide at 121° C. Interestingly,unlike the nickel-chromium-molybdenum alloys with high molybdenumcontents (C-4, C-22, C-276, and C-2000), none of the alloys of thisinvention exhibited a dealloying form of corrosion attack. Alloy C isconsidered borderline in 70% sulfuric acid at 93° C., suggesting that acopper level of 3.1 wt. % is too low (even though Alloy N, with asimilar copper content but higher chromium content, corroded at a lowerrate). The preferred copper range of greater than 3.1 wt. % but no morethan 6.0 wt. % is based on the results for Alloys C and A, respectively.Alloys K and L, with higher copper contents could not be forged.

The chromium range is based on the results for Alloys A and 0 (withcontents of 27 and 33 wt. %, respectively). The molybdenum range isbased on the results for Alloys H and A (with contents of 4.9 and 7.8wt. %, respectively), and the suggestion of U.S. Pat. No. 6,764,646,which indicates that molybdenum contents below 4.9 wt. % do not providesufficient resistance to general corrosion of thenickel-chromium-molybdenum-copper alloys. This is important forneutralizing systems containing other chemicals.

Surprisingly, when iron, manganese, aluminum, silicon, and carbon wereomitted (Alloy G), the alloy could not be forged. To determine furtherthe influence of iron, Alloy P, with no deliberate iron addition, wasmelted. The fact that Alloy P was successfully hot forged and hot rolledindicates that it is the presence of manganese, aluminum, silicon, andcarbon that is critical to the successful wrought processing of thesealloys. In addition, absence of iron in alloy P was not detrimental froma corrosion standpoint as the alloy indicated excellent performance inboth corrosive media.

TABLE 2 Corrosion Test Results for Experimental and Commercial AlloysCorrosion Rate Maximum Internal in 70% H₂SO₄ at Mode of AttackPenetration in 93° C. in 96 h in 50% NaOH at 50% NaOH at 121° C. inAlloy (mm/y) 121° C. in 720 h 720 h (microns) Comments A* 0.44 GC 10[equiv. to 0.12 mm/y] B* 0.32 GC 15 [equiv. to 0.18 mm/y] C 0.48 GC 15[equiv. to 0.18 mm/y] Borderline in H₂SO₄ D 0.64 GC 10 [equiv. to 0.12mm/y] E* 0.35 GC 11 [equiv. to 0.13 mm/y] F* 0.30 GC 12 [equiv. to 0.15mm/y] G — — — Unable to Process H* 0.34 GC 20 [equiv. to 0.24 mm/y] I*0.42 GC  8 [equiv. to 0.10 mm/y] J 1.09 GC 10 [equiv. to 0.12 mm/y] K —— — Unable to Process L — — — Unable to Process M 0.53 GC 17 [equiv. to0.21 mm/y] N 0.42 GC 15 [equiv. to 0.18 mm/y] O* 0.40 GC  8 [equiv. to0.10 mm/y] P* 0.40 GC 13 [equiv. to 0.16 mm/y] Q* 0.39 GC 10 [equiv. to0.12 mm/y] R* 0.41 GC 10 [equiv. to 0.12 mm/y] 200 2.60 GC 13 [equiv. to0.16 mm/y] 400 2.03 GC 14 [equiv. to 0.17 mm/y] 600 7.20 GC 13 [equiv.to 0.16 mm/y] C-4 0.94 Dealloying 69 [equiv. to 0.84 mm/y] C-22 0.94Dealloying 64 [equiv. to 0.78 mm/y] C-276 0.50 Dealloying 58 [equiv. to0.71 mm/y] C-2000 0.37 Dealloying 38 [equiv. to 0.46 mm/y] Borderline inNaOH G-30 0.98 GC  8 [equiv. to 0.10 mm/y] G-35 9.13 GC  8 [equiv. to0.10 mm/y] *denotes an alloy of this invention GC—General Corrosion

The observations regarding the effects of the alloying elements are asfollows:

Chromium (Cr) is a primary alloying element, known to improve theperformance of nickel alloys in oxidizing acids. It has been shown toprovide the desired corrosion resistance to both 70% sulfuric acid and50% sodium hydroxide in the range 27 to 33 wt. %.

Molybdenum (Mo) is also a primary alloying element, known to enhance thecorrosion-resistance of nickel alloys in reducing acids. In the range4.9 to 7.8 wt. %, it contributes to the exceptional performance of thealloys of this invention in 70% sulfuric acid and 50% sodium hydroxide.

Copper (Cu), at levels greater than 3.1 wt. %, but no more than 6.0 wt.%, and in combination with the abovementioned levels of chromium andmolybdenum, produces alloys with unusual and unexpected resistance toacids and alkalis, in the form of 70% sulfuric acid at 93° C. and 50%sodium hydroxide at 121° C.

Iron (Fe) is a common impurity in nickel alloys. Iron contents of up to3.0 wt. % have been found to be acceptable in the alloys of thisinvention.

Manganese (Mn) is used to minimize sulfur in such alloys, and contentsbetween 0.3 and 1.0 wt. % were found to result in successful alloys(from processing and performance standpoints).

Aluminum (Al) is used to minimize oxygen in such alloys, and contentsbetween 0.1 and 0.5 wt. % were found to result in successful alloys.

Silicon (Si) is not normally required in corrosion-resistant nickelalloys, but is introduced during argon-oxygen decarburization (for thosealloys melted in air). A small quantity of silicon (in the range 0.1 to0.8 wt. %) was found to be essential in the alloys of this invention, toensure forgeability.

Likewise, carbon (C) is not normally required in corrosion-resistantnickel alloys, but is introduced during carbon arc melting (for thosealloys melted in air). A small quantity of carbon (in the range 0.01 to0.11 wt. %) was found to be essential in the alloys of this invention,to ensure forgeability.

Traces of magnesium (Mg) and/or rare earth elements are often includedin such alloys for control of unwanted elements, for example sulfur andoxygen. Thus, the usual range of up to 0.05 wt. % is preferred for eachof these elements in the alloys of this invention.

Nitrogen (N) is easily absorbed by high chromium nickel alloys in themolten state, and it is usual to allow a maximum of 0.13 wt. % of thiselement in alloys of this kind.

Other impurities that might occur in such alloys, due to contaminationfrom previously-used furnace linings or within the raw charge materials,include cobalt, tungsten, sulfur, phosphorus, oxygen, and calcium.

If enhanced microstructural stability at elevated temperatures (such asmight be experienced during welding or during elevated temperatureservice) is desired, deliberate, small additions of elements whichencourage the formation of MC carbides can be used. Such elementsinclude titanium, niobium (columbium), hafnium, and tantalum. There areother less desirable MC carbides formers such as vanadium, that could beused. MC carbides are much more stable than the M₇C₃, M₆C, and M₂₃C₆carbides normally encountered in chromium- and molybdenum-containingnickel alloys. Indeed, it should be possible to control the levels ofthese MC-forming elements so as to tie up as much carbon as is deemedsuitable to control the level of carbide precipitation in the grainboundaries. In fact, the MC-former level could be fine-tuned during themelting process, depending upon the real-time measurement of carboncontent.

If the alloy is to be used to resist aqueous corrosion at much lowertemperatures, the MC-former level could be matched to the carbon levelto avoid appreciable grain boundary carbide precipitation (a so-called“stabilized” structure).

There are, however, two potential problems. First, nitrogen is likely tocompete with carbon, resulting in nitrides or carbonitrides of the sameactive former (e.g. titanium), which should therefore be present at ahigher level (this can be calculated based on the real-time measurementof the nitrogen content). Second is the unintended formation ofgamma-prime (with titanium) or gamma-double prime (with niobium) phases;however, it should be possible to adjust the cooling and subsequentprocessing sequences to ensure that these elements are tied up in theform of carbides, nitrides, or carbonitrides.

Ignoring the nitrogen effect and using titanium as an example, to tie upall the carbon in the form of MC carbides would require atomic parity.Since the atomic weight of titanium is approximately four times that ofcarbon (47.9 versus 12.0), this would be reflected in the weightpercentages of the two elements. Thus, stabilized versions of thesealloys for aqueous corrosion service might contain 0.05 wt. % carbon and0.20 wt. % titanium. Those for elevated temperature service mightcontain 0.05 wt. % carbon and 0.15 wt. % titanium, to allow a controlledlevel of secondary, grain boundary precipitation. With nitrogen at animpurity level of 0.035 wt. %, for example, an additional 0.12 wt. %titanium would be necessary to tie up this element (since the atomicweight of nitrogen is 14.0). Thus, with a carbon content of 0.05 wt. %,0.32 wt. % titanium might be required for aqueous corrosion service, and0.27 wt. % titanium might be required for elevated temperature service.Accordingly, with a carbon level of 0.11 wt. %, and a nitrogen impuritylevel of 0.035 wt. %, 0.56 wt. % titanium might be required for aqueouscorrosion service.

The atomic weights of niobium, hafnium, and tantalum are 92.9, 178.5,and 181.0, respectively. Thus, the niobium contents required to reap thesame benefits are approximately double those for titanium. The hafniumor tantalum contents required to reap the same benefits areapproximately quadruple those for titanium.

Accordingly, niobium stabilized versions of these alloys for aqueouscorrosion service might contain 0.05 wt. % carbon and 0.40 wt. % niobium(if the alloy does not contain any nitrogen), and 0.64 wt. % niobium, ifthe nitrogen impurity level is 0.035 wt. %. With a carbon level of 0.11wt. %, and a nitrogen impurity level of 0.035 wt. %, 1.12 wt. % niobiummight be required for aqueous corrosion service. Alloys for elevatedtemperature service, in the absence of nitrogen impurities, mightcontain 0.05 wt. % carbon and 0.30 wt. % niobium.

Likewise, hafnium stabilized versions of these alloys for aqueouscorrosion service might contain 0.05 wt. % carbon and 0.80 wt. % hafnium(if the alloy does not contain any nitrogen), and 1.28 wt. % hafnium, ifthe nitrogen impurity level is 0.035 wt. %. With a carbon level of 0.11wt. %, and a nitrogen impurity level of 0.035 wt. %, 2.24 wt. % hafniummight be required for aqueous corrosion service. Alloys for elevatedtemperature service, in the absence of nitrogen impurities, mightcontain 0.05 wt. % carbon and 0.60 wt. % hafnium.

Likewise, tantalum stabilized versions of these alloys for aqueouscorrosion service might contain 0.05 wt. % carbon and 0.80 wt. %tantalum (if the alloy does not contain any nitrogen), and 1.28 wt. %tantalum, if the nitrogen impurity level is 0.035 wt. %. With a carbonlevel of 0.11 wt. %, and a nitrogen impurity level of 0.035 wt. %, 2.24wt. % tantalum might be required for aqueous corrosion service. Alloysfor elevated temperature service, in the absence of nitrogen impurities,might contain 0.05 wt. % carbon and 0.60 wt. % tantalum.

Prior art concerning other high-chromium nickel alloys (U.S. Pat. No.6,740,291, Crook) indicates that impurity levels of cobalt and tungstenin alloys of this kind can be tolerated at levels up to 5 wt. % and 0.65wt. %, respectively. The acceptable impurity levels for sulfur (up to0.015 wt. %), phosphorus (up to 0.03 wt. %), oxygen (up to 0.05 wt. %),and calcium (up to 0.05 wt. %) are defined in U.S. Pat. No. 6,740,291.These impurity limits are deemed appropriate for the alloys of thisinvention.

Even though the samples tested were in the form of wrought sheets, thealloys should exhibit comparable properties in other wrought forms, suchas plates, bars, tubes, and wires, and in cast and powder metallurgyforms. Also, the alloys of this invention are not limited toapplications involving the neutralization of acids and alkalis. Indeed,they might have much broader applications in the chemical processindustries and, given their high chromium and the presence of copper,should be useful in resisting metal dusting.

Given a desire to maximize the corrosion resistance of these alloys,while optimizing their microstructural stability (hence ease of wroughtprocessing), it is anticipated that the ideal alloy would comprise 31wt. % chromium, 5.6 wt. % molybdenum, 3.8 wt. % copper, 1.0 wt. % iron,0.5 wt. % manganese, 0.3 wt. % aluminum, 0.4 wt. % silicon, and 0.03 to0.07 wt. % carbon, with a balance of nickel, nitrogen, impurities, andtraces of magnesium and the rare earth elements (if used for the controlof sulfur and oxygen). In fact, two alloys, Q and R, with this preferrednominal composition have been successfully melted, hot forged and rolledinto sheet. As seen from Table 2, both alloys Q and R exhibitedexcellent corrosion resistance in the selected corrosive media.Moreover, with this aim nominal composition, a production scale heat(13,608 kg.) of alloy S has been melted and rolled successfully, therebyconfirming that the alloy has excellent formability. A correspondingrange (typical of melt shop practice) would be 30 to 33 wt. % chromium,5.0 to 6.2 wt. % molybdenum, 3.5 to 4.0 wt. % copper, up to 1.5 wt. %iron, 0.3 to 0.7 wt. % manganese, 0.1 to 0.4 wt. % aluminum, 0.1 to 0.6wt. % silicon, and 0.02 to 0.10 wt. % carbon, with a balance of nickel,nitrogen, impurities, and traces of magnesium and the rare earths (ifused for the control of sulfur and oxygen).

What is claimed is:
 1. A nickel-chromium-molybdenum-copper alloyresistant to 70% sulfuric acid at 93° C. and 50% sodium hydroxide at121° C., consisting essentially of: 27 to 33 wt. % chromium 4.9 to 7.8wt. % molybdenum greater than 3.1 wt. % but no more than 6.0 wt. %copper up to 3.0 wt. % iron 0.3 to 1.0 wt. % manganese 0.1 to 0.5 wt. %aluminum 0.1 to 0.8 wt. % silicon 0.01 to 0.11 wt. % carbon up to 0.13wt. % nitrogen up to 0.05 wt. % magnesium up to 0.05 wt. % rare earthelements up to 0.56 wt. % titanium up to 1.12 wt. % niobium up to 2.24wt. % tantalum up to 2.24 wt. % hafnium with a balance of nickel andimpurities.
 2. The nickel-chromium-molybdenum-copper alloy of claim 1,wherein the impurities comprise levels of at least one of cobalt,tungsten, sulfur, phosphorus, oxygen, and calcium.
 3. Thenickel-chromium-molybdenum-copper alloy of claim 1, wherein the alloysare in wrought forms selected from the group consisting of sheets,plates, bars, wires, tubes, pipes, and forgings.
 4. Thenickel-chromium-molybdenum-copper alloy of claim 1, wherein the alloy isin cast form.
 5. The nickel-chromium-molybdenum-copper alloy of claim 1,wherein the alloy is in powder metallurgy form.
 6. Thenickel-chromium-molybdenum-copper alloy of claim 1, consistingessentially of: 30 to 33 wt. % chromium 5.0 to 6.2 wt. % molybdenum 3.5to 4.0 wt. % copper up to 1.5 wt. % iron 0.3 to 0.7 wt. % manganese 0.1to 0.4 wt. % aluminum 0.1 to 0.6 wt. % silicon 0.02 to 0.10 wt. % carbon7. The nickel-chromium-molybdenum-copper alloy of claim 1, consistingessentially of: 31 wt. % chromium 5.6 wt. % molybdenum 3.8 wt. % copper1.0 wt. % iron 0.5 wt. % manganese 0.4 wt. % silicon 0.3 wt. % aluminum0.03 to 0.07 wt. % carbon with a balance of nickel, nitrogen,impurities, and trace amounts of magnesium.
 8. Thenickel-chromium-molybdenum-copper alloy of claim 1, consistingessentially of: 31 wt. % chromium 5.6 wt. % molybdenum 3.8 wt. % copper1.0 wt. % iron 0.5 wt. % manganese 0.4 wt. % silicon 0.3 wt. % aluminum0.03 to 0.07 wt. % carbon with a balance of nickel, nitrogen,impurities, trace amounts of magnesium and trace amounts of the rareearth elements.
 9. The nickel-chromium-molybdenum-copper alloy of claim1, wherein the alloy contains at least one MC carbide former.
 10. Thenickel-chromium-molybdenum-copper alloy of claim 9, wherein the MCcarbide former is selected from the group consisting of titanium,niobium, tantalum and hafnium.
 11. The nickel-chromium-molybdenum-copperalloy of claim 1, wherein the alloy contains 0.20 to 0.56 wt. %titanium.
 12. The nickel-chromium-molybdenum-copper alloy of claim 1,wherein the alloy contains 0.30 to 1.12 wt. % niobium.
 13. Thenickel-chromium-molybdenum-copper alloy of claim 1, wherein the alloycontains 0.60 to 2.24 wt. % tantalum.
 14. Thenickel-chromium-molybdenum-copper alloy of claim 1, wherein the alloycontains 0.60 to 2.24 wt. % hafnium.